EP3437781A1 - Verfahren und vorrichtung zum rührreibschweissen von baustahl - Google Patents

Verfahren und vorrichtung zum rührreibschweissen von baustahl Download PDF

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Publication number
EP3437781A1
EP3437781A1 EP17774532.0A EP17774532A EP3437781A1 EP 3437781 A1 EP3437781 A1 EP 3437781A1 EP 17774532 A EP17774532 A EP 17774532A EP 3437781 A1 EP3437781 A1 EP 3437781A1
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EP
European Patent Office
Prior art keywords
rotary tool
friction stir
surface side
stir welding
rotary
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Granted
Application number
EP17774532.0A
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English (en)
French (fr)
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EP3437781B1 (de
EP3437781A4 (de
Inventor
Muneo Matsushita
Rinsei Ikeda
Koichi Taniguchi
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JFE Steel Corp
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JFE Steel Corp
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Publication of EP3437781A4 publication Critical patent/EP3437781A4/de
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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
    • B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
    • B23K20/123—Controlling or monitoring the welding process
    • B23K20/1235—Controlling or monitoring the welding process with temperature control during joining
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
    • B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
    • B23K20/1245—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding characterised by the apparatus
    • B23K20/125—Rotary tool drive mechanism
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/12—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding
    • B23K20/122—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding
    • B23K20/1245—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating the heat being generated by friction; Friction welding using a non-consumable tool, e.g. friction stir welding characterised by the apparatus
    • B23K20/1255—Tools therefor, e.g. characterised by the shape of the probe
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K20/00—Non-electric welding by applying impact or other pressure, with or without the application of heat, e.g. cladding or plating
    • B23K20/24—Preliminary treatment
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2101/00—Articles made by soldering, welding or cutting
    • B23K2101/18—Sheet panels
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K2103/00—Materials to be soldered, welded or cut
    • B23K2103/02—Iron or ferrous alloys
    • B23K2103/04—Steel or steel alloys

Definitions

  • the present invention relates to a friction stir welding method for welding workpieces without the addition of a filler metal, the method including:
  • the method uses plastic flow generated by stirring the softened portion with the rotary tool.
  • the present invention also relates to an apparatus that can provide the method.
  • Patent Literature 1 discloses a technique for welding metal materials (workpieces), in which, by rotating at least one of a pair of metal materials, the metal materials are softened by frictional heat generated there, and the softened portion is stirred to produce plastic flow, thereby the metal materials can be welded.
  • Patent Literature 2 discloses a method for continuously welding workpieces in the longitudinal direction thereof using heat generated between the workpieces and a tool and plastic flow caused by inserting the tool into a non-welded part of the workpieces and moving the tool while rotating the tool.
  • the tool is made of a material substantially harder than the material of the workpieces.
  • the friction welding method disclosed in Patent Literature 1 involves welding workpieces with frictional heat generated between the workpieces while rotating the workpieces.
  • the friction stir welding method disclosed in Patent Literature 2 can weld the workpieces by moving and rotating the tool while the workpieces are fixed. Therefore, this method has an advantage of continuous solid-state welding of workpieces in the longitudinal direction, even if the workpieces are substantially infinitely long in the welding direction. Since this method provides solid-state welding using plastic flow of metal produced by frictional generated heat between the rotary tool and the workpieces, the workpieces can be welded together without the need to melt the non-welded part. Furthermore, this method has many advantages of, for example, less deformation after welding because of heating temperature by heating means being low, fewer welded-part defects because of the non-welded part staying not molten, no necessity for a filler metal and so forth.
  • non-welded part refers to an abutting portion, for example, between steel sheets that merely abut each other and are not welded.
  • welded part refers to a portion welded and integrated by plastic flow.
  • the friction stir welding method has a wide range of applications in the fields pertaining to aircraft, watercraft, railed vehicles, and motor vehicles, and other fields as a method for welding low-melting-point metal materials typified by aluminum alloys and magnesium alloys.
  • the reason for this is that an arc welding process known in the art is unlikely to provide the welded part of such low-melting-point metal materials with satisfactory properties, and the use of the friction stir welding method improves productivity and the quality of the welded part.
  • the use of the friction stir welding method for structural steel mainly used as a material for structures such as buildings, watercraft, heavy machines, pipelines, and motor vehicles avoids solidification cracking and hydrogen cracking, which are problematic in fusion welding known in the art, and also suppresses microstructural changes in steel, which is expected to improve joint performance.
  • the friction stir welding method also has an anticipated advantage of no necessity for a preparation step, such as diffusion welding, because stirring the joint interface with the rotary tool creates clean surfaces and enables contact between the clean surfaces. Consequently, the use of the friction stir welding method for structural steel has many anticipated advantages. However, challenges associated with welding workability, such as suppression of defect generation during welding and an increase in welding speed remain, which hinders the friction stir welding method from being used widely for structural steel compared with low-melting-point metal materials.
  • Patent Literatures 5 to 7 disclose welding methods using additional heating means in addition to frictional heat generated between a rotary tool and workpieces in order to improve welding workability.
  • Patent Literature 5 discloses a friction stir welding method involving heating means using an induction heating device, which heats workpieces before and after welding to increase the welding speed and prevent or reduce cracking in the welded part.
  • Patent Literature 6 discloses a friction stir welding apparatus having heating means using a laser device, which partially heats workpieces just before welding to reduce changes in microstructure around the region heated by preheating and to increase the welding speed.
  • Patent Literature 7 discloses a friction stir welding apparatus having heating means using a laser device, which partially heats workpieces just before welding. When heating is performed, the surface temperature, depth, and so forth of the heated region of the workpieces are strictly controlled. Thus, plastic flow deficiency as a result of insufficient heating of the workpieces is eliminated, sufficient strength is given, and the welding workability can be improved.
  • Patent Literatures 8 and 9 disclose both-side friction stir welding methods and apparatuses in which rotary tools are provided on upper and lower sides one by one, and the rotary tools are disposed to vertically face the front surface side and the back surface side of overlapping portions of two metal sheets.
  • the both-side friction stir welding methods and apparatuses workpieces are pressed from the upper and lower sides while the rotary tools are rotated, and the workpieces are welded while the rotary tools are moved in the welding direction. Accordingly, welding defects are suppressed and the welding strength can be increased. Further, by increasing the life of rotary tools, the economy of the rotary tools can be improved.
  • the heating source exists only on one surface side (for example, front surface side).
  • the temperature is lower on the side opposite to the side provided with the heating means and the rotary tool, that is, the back surface side, compared with the temperature on the front surface side.
  • a temperature difference is generated in the thickness direction of the workpieces from the front surface side to the back surface side.
  • the strength of the metal sheets used as the workpieces decreases as the temperature increases.
  • the load on the rotary tool during friction stir welding may decrease as the temperature increases.
  • the load applied to the distal end of the pin of the rotary tool may be decreased by eliminating the temperature difference that is generated in the thickness direction of the workpieces.
  • Patent Literatures 5 to 7 do not consider at all the decrease in the load on the rotary tool by eliminating the temperature difference in the thickness direction of the workpieces.
  • the both-side friction stir welding methods disclosed in Patent Literatures 8 and 9 may be effective.
  • the welding methods do not consider at all the decrease in the load on the rotary tool, the improvement in the welding workability, and the increase in the life of the rotary tool by the preheating process for heating the workpieces using the heating means in front of the rotary tool.
  • the present invention has been developed in light of the above-mentioned circumstances.
  • An object of the present invention is to obtain a welded part having sufficient strength and improve welding workability by eliminating plastic flow deficiency generated as a result of insufficient heating of workpieces during friction stir welding for structural steel.
  • the present invention therefore provides a friction stir welding method and a friction stir welding apparatus capable of performing a preheating process under particularly strictly specified conditions.
  • the inventors of the present invention have obtained the following findings as a result of diligent studies to solve the above-mentioned problems.
  • the preheating process before friction stir welding is considered to be effective.
  • the inventors have carried out various studies on the conditions of the preheating process before friction stir welding.
  • the present invention is based on the above-mentioned findings.
  • the present invention improves welding workability during friction stir welding for structural steel by eliminating plastic flow deficiency generated as a result of insufficient heating of workpieces in the sheet thickness direction, the plastic flow deficiency having been a concern for years.
  • the invention also reduces changes in microstructure to provide high joint strength in the welded part.
  • the present invention provides a friction stir welding method and a friction stir welding apparatus for structural steel.
  • the method and apparatus include a preheating process for heating workpieces (steel sheets) by heating means provided in front of a rotary tool, and a friction stir process using the rotary tool behind the heating means.
  • the rotary tool is arranged on each of one surface (front surface) side and the other surface (back surface) side of the steel sheets to face one another.
  • the rotary tools weld the steel sheets by producing plastic flow as a result of that the steel sheets are softened by frictional heat generated between the steel sheets and the rotary tools during rotation and that the softened portion is stirred with the rotary tools.
  • reference signs 1 and 15 denote rotary tools
  • 2 denotes a rotation axis
  • 3 denotes a steel sheet
  • 4 denotes a welded part
  • 5 denotes heating means
  • 6 denotes cooling means
  • 7 denotes rear reheating means
  • 8 and 16 denote shoulders of the rotary tools
  • 9 and 17 denote pins of the rotary tools
  • ⁇ and ⁇ denote tilt angles of the rotary tools.
  • the advancing side is defined as a side that the rotation direction of the rotary tool (tool rotation direction) on the front surface side provided with the heating means agrees with the welding direction.
  • the retreating side is defined as a side that the tool rotation direction on the front surface side opposes the welding direction.
  • the steel sheets (workpieces) 3, 3 are held by a holding device (not illustrated) from the front and back surface sides, the pins of the facing rotary tools are inserted into a non-welded part from the front surface side and the back surface side of the non-welded part of the workpieces, the shoulders of the facing rotary tools are pressed to the front surface side and the back surface side of the workpieces, and thus welding is performed.
  • a clearance ⁇ may be appropriately provided between the distal ends of the pins of the facing rotary tools so that application of friction by the shoulders and stirring by the pins are properly performed and welding is soundly performed.
  • the clearance ⁇ is effectively 0.1 mm or larger. If the clearance ⁇ is too large, a portion that is not properly stirred by the pins becomes defective.
  • the clearance ⁇ is preferably 0.3 mm or smaller.
  • the facing rotary tools include a shoulder and a pin.
  • the pin is arranged on the shoulder and shares the rotation axis with the shoulder. At least the shoulder and the pin are formed of a material harder than the material of the steel sheets used as workpieces.
  • One of the rotary tools on the one surface side provided with the heating means of the facing rotary tools may include the shoulder but may not include the pin.
  • the shoulder of the rotary tool on the one surface side, and the shoulder and the pin of the rotary tool on the other surface side may be formed of a material harder than the material of steel sheets used as workpieces.
  • the rotary tool has a shape in which the pin having a substantially columnar shape and having a diameter smaller than that of the shoulder is provided on the shoulder having a substantially columnar shape.
  • the surface of the shoulder may also be tapered.
  • a rotary tool in which at least a shoulder and a pin thereof are formed of a material harder than the material of steel sheets used as workpieces is arranged only on the one surface side of the steel sheets, the pin is inserted into a non-welded part of the steel sheets, and welding is performed.
  • the length in the axial direction of the pin (pin length) is required to be equivalent to the thickness of the workpieces.
  • the pin length is preferably smaller.
  • the pin lengths of both the facing rotary tools when the pin lengths of both the facing rotary tools are the same, the pin lengths can be about a half of the thickness of the workpieces.
  • the load to be applied to each rotary tool can be decreased as compared with a case where the pin of the rotary tool is inserted only from the one surface side to perform welding.
  • the load on the rotary tool on the side provided with the heating means is smaller than the pin length of the tool on the opposite side, the load can be decreased owing to the smaller pin length of the rotary tool on the side provided with the heating means.
  • sufficient heat can be supplied by the heating means to the welded part around the distal end of the rotary tool on the side opposite to the side provided with the heating means.
  • the load on the tool can be likewise decreased.
  • the load to be applied to the tools can become component forces compressed in the axial direction.
  • At least the shoulders and the pins of the tools are required to be formed of a material harder than the steel sheets, and therefore, a material having low toughness such as ceramics is used in many cases. If a force is applied to the pins in a bending direction, the force may be concentrated at a local portion, and the pins may be broken.
  • the load on the tools is received as component forces compressed in the axial direction.
  • the force in the bending direction can be decreased, and damage to the tools can be avoided.
  • An example of the tilt angle of each of the pins is in a range from 1° to 5°.
  • the tilt angle of the pin represents one of angles defined between the central axis of the rotary tool and the vertical line and having an acute angle.
  • the preheating process for heating a steel sheet with the heating means provided in front of the rotary tool that moves in the welding direction is important.
  • the conditions of the preheating process will be described below with reference to Fig. 2 .
  • reference sign 10 denotes a welding centerline.
  • the welding centerline is a straight line passing through the rotation axis of the rotary tool and being parallel to the welding direction on the surface of the steel sheet.
  • Reference sign 12 denotes a heated region
  • 13 denotes a cooled region
  • 14 denotes a reheated (rear heated) region
  • a denotes the diameter of the shoulder of the rotary tool
  • b denotes the maximum diameter of the pin of the rotary tool
  • X denotes the minimum distance between the heated region and the rotary tool
  • D denotes the depth of the heated region
  • t denotes the thickness of the steel sheet.
  • Fig. 3 illustrates the relationship between the temperature and the tensile strength of the steel sheet to be welded by the friction stir welding method and apparatus according to the present invention.
  • the steel sheet normally has a strength of about 30% of room-temperature strength at a temperature of about 80% of T A1 (ferrite-austenite transformation temperature), which is the transformation temperature of steel. As the temperature is higher than about 80% of T A1 , the steel sheet has lower strength.
  • the steel sheet is softened in advance by increasing the surface temperature of the steel sheet to 0.8 ⁇ T A1 °C or higher, and the softened portion of the steel sheet is stirred to accelerate plastic flow, which reduces the load on the rotary tool and increases the welding speed.
  • the surface temperature T S (°C) of the steel sheet in the heated region is set to 0.8 ⁇ T A1 °C or higher.
  • the temperature T A1 (°C) can be obtained from Formula (1) below.
  • T A 1 ° C 723 ⁇ 10.7 % Mn ⁇ 16.9 % Ni + 29.1 % Si + 16.9 % Cr + 290 % As + 6.38 % W
  • [%M] represents a content (mass%) of an M element in the steel sheet used as a workpiece. If the M element is not contained, [%M] is 0.
  • the surface of the heated region may have a temperature gradient.
  • the surface temperature of the steel sheet in the heated region is preferably 1.5 ⁇ T M °C or lower.
  • the surface temperature of the steel sheet in the heated region is preferably lower than T M °C until the heated region contacts the rotary tool passing through the heated region.
  • the temperature T M (°C) is a melting point of the steel sheet used as a workpieces.
  • the minimum distance between the heated region on the surface of the steel sheet and the rotary tool that moves in the welding direction is set to a distance equal to or smaller than the diameter of the shoulder of the rotary tool.
  • the minimum distance between the heated region on the surface of the steel sheet and the rotary tool that moves in the welding direction is preferably set to 0.1 times or more of the diameter of the shoulder of the rotary tool.
  • the moving speed of the rotary tool is preferably in a range from 200 mm/min to 3000 mm/min.
  • the diameter of the shoulder of the rotary tool is about 8 to 60 mm.
  • the heated region is too large, the microstructures of the heated region and the surrounding region change.
  • heating at the ferrite-austenite transformation temperature or lower still tempers martensite to cause softening and thus significantly reduces the welded part strength.
  • the area of the heated region on the surface of the steel sheet is set to an area equal to or smaller than the area of the maximum diameter part of the pin of the rotary tool.
  • the area of the heated region on the surface of the steel sheet is preferably 0.1 times or more of the area of the maximum diameter part in the pin of the rotary tool.
  • the maximum diameter of the pin (pin diameter) of the rotary tool is about 2 to 50 mm.
  • the maximum diameter of the pin of the rotary tool is the largest diameter among diameters that are obtained at cross sections when a single pin is cut at cross sections (a plurality of times) perpendicular to the axial direction. For example, as illustrated in Fig. 4(1) to 4(4) , if the diameter of the pin does not change along the axial direction, the diameter of the upper surface of the pin (in the drawing, 4 mm) can be considered as the maximum diameter of the pin. If the pin has a tapered shape or the like and the diameter of the pin varies depending on the position in the axial direction, the largest diameter among diameters that are obtained at a plurality of cross sections can be considered as the maximum diameter.
  • the shape of the heated region can be any shape, such as a circular shape, an ellipsoidal shape, or a quadrangular shape.
  • the area of the heated region is calculated, if the shape of the heated region is an ellipsoidal shape, the major axis thereof can be employed as the pin diameter, and if the shape is a quadrangular shape or the like, the diameter of the equivalent circle can be employed as the pin diameter.
  • the steel sheet to be welded with the friction stir welding method and apparatus of the present invention normally has a strength of about 30% of room-temperature strength at a temperature of about 80% of T A1 , which is the transformation temperature of steel. As the temperature is higher than about 80% of T A1 , the steel sheet has lower strength. Hence, it is preferable to increase the temperature of the steel sheet not only at the surface of the steel sheet but also in the thickness direction and soften the steel sheet in advance. To be specific, the steel sheet is preferably softened in advance by keeping the temperature at 0.8 ⁇ T A1 °C or higher even in the thickness direction of the heated region.
  • the temperature T D of the heated region in the thickness direction which defines the depth D of the heated region described below, is set to 0.8 ⁇ T A1 °C or higher.
  • the temperature T A1 (°C) can be obtained from Formula (1) below.
  • T A 1 ° C 723 ⁇ 10.7 % Mn ⁇ 16.9 % Ni + 29.1 % Si + 16.9 % Cr + 290 % As + 6.38 % W
  • [%M] represents a content (mass%) of an M element in the steel sheet used as a workpiece. If the M element is not contained, [%M] is 0.
  • the heated region may have a temperature gradient in the thickness direction.
  • the temperature of the steel sheet in the heated region in the thickness direction is preferably 1.5 ⁇ T M °C or lower during heating with the heating means.
  • the temperature of the steel sheet in the heated region in the thickness direction is preferably lower than T M °C until the heated region contacts the rotary tool passing through the heated region.
  • the temperature T M (°C) is a melting point of the steel sheet used as a workpiece.
  • the depth D of the heated region is defined as the maximum depth of a region that has a temperature T D of 0.8 ⁇ T A1 °C or higher in the heated region in the thickness direction and that extends from the surface of the steel sheet used as a workpiece.
  • the depth D of the heated region is preferably 100% of the thickness of the steel sheet.
  • Control means for controlling operating conditions of the apparatus may also be used so that the position and area of the heated region satisfy the above-described conditions (condition 1) or the depth D of the heated region satisfies the above-described conditions (condition 2).
  • the control means can control the operating conditions of the heating means and the rotary tools.
  • the control means can also control the operations of, for example, rear heating means, cooling means, and rear reheating means (described later).
  • plastic flow on the front surface side starts from the advancing side, moves along the rotation direction of the rotary tool, passes sequentially through the front side in the welding direction, through the retreating side, and through the rear side in the welding direction, and ends on the advancing side.
  • the material forming the surface of the rotary tool preferably has a kinetic friction coefficient with respect to the steel sheet being larger than 0.6.
  • the rotary tool may be formed of a material whose kinetic friction coefficient with respect to the steel sheet is larger than 0.6, or the surface of the rotary tool may be coated with a material whose kinetic friction coefficient with respect to the steel sheet is larger than 0.6.
  • the material is only required to be formed on at least a surface of the rotary tool, the surface which contacts the steel sheet during friction stirring.
  • the material whose kinetic friction coefficient with respect to the steel sheet is larger than 0.6 may be, for example, tungsten carbide (WC).
  • the method for measuring the kinetic friction coefficient is not limited to a particular method, but may use, for example, a ball-on-disk method.
  • the heating means used in the preheating process is not limited to a particular device, but a laser heating device is preferably used.
  • the conditions other than the above-described conditions are not limited and, for example, the moving speed of the heating means used in the preheating process is set to substantially the same as the welding speed.
  • the laser output, the beam diameter, and so forth are set appropriately according to the welding conditions.
  • cooling means is provided behind the rotary tool that moves in the welding direction, and the cooling means can improve the welded part strength.
  • the welded part is normally cooled naturally after completion of welding, and thus there has been a problem in that sufficient welded part strength is not obtained when steel used as a workpiece has low hardenability.
  • the cooling means provided behind the rotary tool that moves in the welding direction can cool the welded part of the steel sheet, and appropriate control of the cooling rate allows the strength to be improved by quench hardening.
  • Specific cooling means is preferably cooling means using jet spraying of inert gas.
  • the cooling rate in this case is preferably, for example, 30°C/s to 300°C/s in the range of 800°C to 500°C.
  • the inert gas may be, for example, argon gas, helium gas, or other gas.
  • Rear reheating means may be provided behind the rotary tool that moves in the welding direction and behind the cooling means described above.
  • the rear reheating means may reheat the welded part of the steel sheets.
  • the hardness can be reduced by tempering the welded part with the rear reheating means to obtain good joint properties, namely, both high strength and toughness.
  • the cooling rate by the cooling means in this case is preferably, for example, 30°C/s to 300°C/s in the range of 800°C to 500°C.
  • the temperature of the welded part after the reheating is preferably, for example, from 550°C to 650°C.
  • Cooling means may be provided behind the rotary tool that moves in the welding direction and behind the rear reheating means described above; thereby the welded part of the steel sheets be cooled.
  • a composite microstructure can be formed by, just after welding, reducing the cooling rate with the rear reheating means and then increasing the cooling rate with the cooling means, which provides good joint properties, namely, both high strength and high ductility.
  • the cooling rate by the reheating means in this case is preferably about 10°C/s to 30°C/s in the range of 800°C to 600°C, and then the cooling rate by the cooling means is preferably about 30°C/s to 300°C/s in the range of 600°C to 400°C.
  • the welding conditions other than the above-described conditions are set according to an ordinary method.
  • a larger torque of the rotary tool means lower plastic flowability of the steel sheets and results in higher tendency to generate defects or the like.
  • attempts are preferably made to regulate the torque of the rotary tool by controlling the rotation speed of the rotary tool in the range of 100 to 1000 rpm and to increase the welding speed to 1000 mm/min or higher.
  • general structural steel or carbon steel such as rolled steel for weld structure of JIS (Japan Industrial Standards) G 3106 or carbon steel for machine structure of JIS G 4051, can be suitably used.
  • the present invention can also be advantageously applied to high-strength structural steel having tensile strength of 800 MPa or higher.
  • the strength of the welded part is equal to or higher than 85% of the tensile strength of the steel sheet (base material) or even equal to or higher than 90% of the tensile strength of the steel sheet (base material).
  • Friction stir welding was performed using steel sheets (steel sheets 1 together or steel sheets 2 together) having a sheet thickness of 1.60 mm and having the chemical compositions (residual parts other than the compositions in Table 1 are composed of Fe and unavoidable impurities) and the tensile strengths shown in Table 1.
  • the welding conditions for friction stir welding are shown in Table 2 (and Table 5).
  • Conditions L4 and H3 are welding conditions when welding was performed while a rotary tool was pressed from the one surface side of the steel sheets (comparative examples).
  • Conditions L1, L2, L3, H1, and H2 are welding conditions when welding was performed while rotary tools were pressed from both the one surface side and the other surface side (examples of the present invention, or referred to as invention examples) of the steel sheets.
  • a rotary tool made of tungsten carbide (WC) and having one of four shapes with the cross-sectional dimensions shown in Figs. 4(1), 4(2), 4(3), and 4(4) was used. During welding, oxidation of the surface was prevented by shielding the welded part with argon gas.
  • tungsten carbide for a material of the surface of the rotary tool, one using tungsten carbide (WC) as a base material and not coated (Invention Examples 1 to 24 and Comparative Examples 1 to 7) or one using tungsten carbide as a base material and coated with titanium nitride (TiN) by physical vapor deposition (PVD) (WC+TiN) (Invention Examples 25 to 27) was used.
  • the friction coefficient between the surface of the rotary tool and the steel sheet was 0.7 in the case without coating on WC, and 0.5 in the case with TiN coating.
  • the steel sheet 1 shown in Table 1 was irradiated with a laser beam under different irradiation conditions (laser moving speed, laser output, and beam diameter) shown in Table 3, and the surface temperature was measured by thermography. Microstructure observation using a Nital etching solution was carried out by observing the cross section of the laser-irradiated part.
  • the region having temperatures equal to or higher than the transformation temperature (T A1 °C) was etched most deeply, and its surrounding region where the temperature was lower than the transformation temperature (T A1 °C) but the structure with high hardness such as martensite in the base material was tempered was etched relatively shallowly.
  • the region having experienced temperatures equal to or higher than the transformation temperature (T A1 °C), the region tempered at temperatures lower than the transformation temperature (T A1 °C), and the base-material region can be distinguished from each other.
  • the region tempered at temperatures lower than the transformation temperature (T A1 °C) corresponds to the region having temperatures of 0.8 ⁇ T A1 °C or higher and lower than T A1 °C.
  • the depth D 0 of the region having experienced temperatures equal to or higher than the transformation temperature (T A1 °C) and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C (the depth D of the heated region) were determined by such microstructure observation using a Nital etching solution.
  • the measurement results of the surface temperature by thermography indicate that, under the irradiation condition A, the region having temperatures equal to or higher than 0.8 ⁇ T A1 °C had a circular shape with a diameter of 2.4 mm. Since the maximum diameter of the pin of the rotary tool used here is 4.0 mm, the area of the heated region on the surface of the steel sheet is equal to or smaller than the area of the maximum diameter part of the pin of the rotary tool.
  • the region having temperatures equal to or higher than 0.8 ⁇ T A1 °C had a circular shape with a diameter of 2.0 mm. Therefore, the area of the heated region on the surface of the steel sheet is equal to or smaller than the area of the maximum diameter part of the pin of the rotary tool similarly as described above.
  • the region having temperatures equal to or higher than 0.8 ⁇ T A1 °C had a circular shape with a diameter of 5.4 mm. Since the maximum diameter of the pin of the rotary tool used here is 4.0 mm, the area of the heated region on the surface of the steel sheet is larger than the area of the maximum diameter part of the pin of the rotary tool. In any of the irradiation conditions A to C, the heated region had a circular shape, and hence the minor axis thereof is not described in Table 4.
  • the region having temperatures equal to or higher than 0.8 ⁇ T A1 °C had an ellipsoidal shape with a major diameter of 1.8 mm in the laser moving direction, and a minor diameter of 1.2 mm in the direction perpendicular to the laser moving direction. Since the maximum diameter of the pin of the rotary tool used here is 4.0 mm, the area of the heated region on the surface of the steel sheet is equal to or smaller than the area of the maximum diameter part of the pin of the rotary tool.
  • the region having temperatures equal to or higher than 0.8 ⁇ T A1 °C had an ellipsoidal shape with a major diameter of 2.3 mm in the laser moving direction, and a minor diameter of 1.9 mm in the direction perpendicular to the laser moving direction. Therefore, the area of the heated region on the surface of the steel sheet is equal to or smaller than the area of the maximum diameter part of the pin of the rotary tool similarly as described above.
  • the depth Do of the region having experienced temperatures equal to or higher than T A1 °C and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C were 1.60 mm and 1.60 mm, respectively.
  • the region having experienced temperatures equal to or higher than T A1 °C was formed in the entire thickness of the steel sheet. Therefore, the depth D of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C is 100% of the thickness t of the steel sheet.
  • the depth Do of the region having experienced temperatures equal to or higher than T A1 °C and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C (the depth D of the heated region) were 0.47 mm and 0.50 mm, respectively. Since the thickness t of the steel sheet used as a workpiece is 1.60 mm, the depth D of the heated region is about 31.3% of the thickness t of the steel sheet.
  • the depth Do of the region having experienced temperatures equal to or higher than T A1 °C and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C (the depth D of the heated region) were 0.28 mm and 0.30 mm, respectively. Since the thickness t of the steel sheet used as a workpiece is 1.60 mm, the depth D of the heated region is about 18.8% of the thickness t of the steel sheet.
  • the depth Do of the region having experienced temperatures equal to or higher than T A1 °C and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C were 1.60 mm and 1.60 mm, respectively.
  • the region having temperatures equal to or higher than T A1 °C was formed in the entire thickness of the steel sheet. Therefore, the depth D of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C is 100% of the thickness t of the steel sheet.
  • the depth Do of the region having experienced temperatures equal to or higher than T A1 °C and the depth of the region having experienced temperatures equal to or higher than 0.8 ⁇ T A1 °C (the depth D of the heated region) were 0.58 mm and 0.63 mm, respectively. Since the thickness t of the steel sheet used as a workpiece is 1.60 mm, the depth D of the heated region is about 39.4% of the thickness t of the steel sheet.
  • Table 5 shows the conditions of the preheating process by laser irradiation before welding of the workpieces and the conditions of the process after welding.
  • cooling was performed by gas jet spraying and heating (and reheating) was performed by induction heating.
  • Table 6 shows the measurement values of the torque of the rotary tool during welding and the tensile strength of the obtained weld joint.
  • the tensile strength was determined by performing tensile testing on tensile test specimens that were taken from the obtained weld joint and had the size of specimen no. 1 defined in JIS Z 3121.
  • Table 6 shows that, in Invention Examples 1 to 11, a welding speed of 400 mm/min still resulted in a strength corresponding to 85% or higher of the tensile strength of the steel sheet used as a base material as well as a torque of the rotary tool on each of the front surface side and the back surface side of 80 N ⁇ m or smaller, which indicates good plastic flowability.
  • Invention Examples 7 and 8 involving cooling and reheating after welding exhibited a strength corresponding to 99% or higher of the tensile strength of the base material.
  • Comparative Examples 1 to 3 were performed under the friction stir welding conditions for welding by pressing the rotary tools from both the one surface side and the other surface side of the steel sheet satisfying the ranges of the present invention, the welding speed was 400 mm/min, and the conditions for preheating process did not satisfy the ranges of the present invention.
  • the torque of the rotary tool on each of the front surface side and the back surface side was larger than 80 N ⁇ m, which indicates poor plastic flowability.
  • Comparative Example 4 was performed under the friction stir welding conditions for welding by pressing the rotary tool from only the one surface side of the steel sheets not satisfying the ranges of the present invention, and the conditions for preheating process satisfied the ranges of the present invention. But the torque of the rotary tool on the front surface side was larger than 80 N ⁇ m, which indicates poor plastic flowability.
  • Table 6 shows that, in Invention Examples 12 to 21, a high welding speed of 1000 mm/min still resulted in welding with a strength corresponding to 85% or higher of the tensile strength of the steel sheet used as a base material as well as a torque of the rotary tool on each of the front surface side and the back surface side of 100 N ⁇ m or smaller, providing a sound joint.
  • Invention Examples 17 and 18 involving cooling and reheating after welding exhibited a strength corresponding to 100% of the tensile strength of the base material.
  • Comparative Examples 5 and 6 were performed under the friction stir welding conditions for welding by pressing the rotary tools from both the one surface side and the other surface side of the steel sheets satisfying the ranges of the present invention and the conditions for preheating process did not satisfy the ranges of the present invention.
  • Comparative Example 7 was performed under the friction stir welding conditions for welding by pressing the rotary tool from only the one surface side of the steel sheet not satisfying the ranges of the present invention and the conditions for preheating process satisfy the ranges of the present invention. In Comparative Examples 5 to 7, a non-welded part remained, welding was not performed, and a sound joint was not obtained. Therefore, the measurements on the torque and so force of the rotary tools were not performed in Comparative Examples 5 to 7.
  • Table 6 shows that, in Invention Examples 22 to 24, a high welding speed of 1000 mm/min still resulted in normal welding with a torque on each of the front surface side and the back surface side of the rotary tool of 95 N ⁇ m or smaller.
  • Invention Examples 22 to 24 exhibited a strength corresponding to 90% or more of the tensile strength of the steel sheet used as a base material. A sound joint was obtained.
  • Invention Examples 25 to 27 using a material with a kinetic friction coefficient with respect to the steel sheet of 0.6 or smaller the torque of the rotary tool on each of the front surface side and the back surface side was 76 N ⁇ m or smaller.
  • Invention Examples 25 to 27 exhibited a strength corresponding to 75% to 80% of the tensile strength of the steel sheet used as a base material, which indicates a poor joint compared to the sound joint in Invention Examples 22 to 24 experimented under the same conditions except for the kinetic friction coefficient.

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  • Engineering & Computer Science (AREA)
  • Mechanical Engineering (AREA)
  • Pressure Welding/Diffusion-Bonding (AREA)
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WO2017169991A1 (ja) 2017-10-05
EP3437781B1 (de) 2022-02-09
US20200306871A1 (en) 2020-10-01
CN109070262A (zh) 2018-12-21
EP3437781A4 (de) 2019-06-12
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CN109070262B (zh) 2021-09-10
US11241755B2 (en) 2022-02-08

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